CN1724469A - Method for manufacturing multi-element ceramic powder and sintered compact - Google Patents
Method for manufacturing multi-element ceramic powder and sintered compact Download PDFInfo
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Abstract
The invention provides a preparation method of polynary system ceramic powder, including the following steps: production through mechanical blending of powdered alloy with the components of at least one of W and Cr, Ti, Zr, and Hf, and at least one of V, Nb, and Ta; heating of the powdered alloy, the carbon powder material and the catalyst in nitrogen atmosphere, to nitrocarburize into polynary system ceramic powder; sintering the polynary system ceramic powder to prepare another polynary system ceramic powder. The invention provides a method to prepare another polynary system ceramic powder, including the following steps: producing the formed body through the preparation of the powder of a first material with the components of at least two material elements of Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, and W; wrapping the formed body with a second material with the components of metal elements which are not contained in the first material, and heating in N atmosphere; smashing the porous sintered body produced in such a way to produce the polynary system ceramic powder. When preparing the sintered body, the formed body can be heated at a sintering temperature of the formed body.
Description
The application is that international filing date is that June 27, China national application number in 2002 are 02813293.9, denomination of invention is divided an application for the application of " polynary system ceramic powder and manufacture method thereof and sintered compact and manufacture method thereof ".
Technical field
The present invention relates to also comprise with several metal element and N, sometimes C is polynary system ceramic powder and manufacture method and sintered compact and the manufacture method thereof that constitutes element.
Background technology
Both had the high tenacity that comes from metal by the matrix material that metal-powder and ceramic powder sintering are together made, had the high rigidity and the high strength that come from pottery again, and therefore in various fields, obtained using widely.For example, the WC-Co that is formed by wolfram varbide (WC) and cobalt (Co) sintering is that superhard alloy and the TiC that formed by titanium carbide (TiC) and molybdenum (Mo) sintering are the cutlery that sintering metal is used as cutting tool.Sometimes also in these materials, cooperate niobium carbide (NbC) etc.
Be above-mentioned WC or TiC, NbC etc. with a kind of metallic element and C as the ceramic powder of matrix material raw material serve as that to constitute the two component system carbide ceramics of element or TiN etc. be the two component system nitride ceramics etc. that constitutes element with a kind of metallic element and N.These materials himself have enough hardness, but also wish to have more high-hardness ceramic according to the needs of purposes sometimes.
The high rigidity pottery comprises for example diamond or tetragonal spheroidal boron nitride (c-BN) etc.In addition, also report with Ti, Al and N to serve as that the film that constitutes the Ti-Al-N ternary system ceramics of element has the high rigidity that is equal to mutually with c-BN in recent years.That is, the hardness of Ti-Al-N ternary system ceramics is significantly higher than the hardness of TiN or AlN, and also higher than the hardness of TiN and the AlN resulting sintered compact of sintering together.
The film of Ti-Al-N ternary system ceramics (PVD) method or chemical vapor deposition (CVD) method of can growing up with physical vapor is made.
Because scale resistance is bad and price is high, so diamond or c-BN have the disadvantage that the matrix material manufacturing cost is increased sharply.Therefore,, consider as the Ti-Al-N ternary system ceramics that using two or more metallic elements and C or N is effective for the polynary system ceramic powder that constitutes element as raw material in order to make matrix material chemically stable and that have high rigidity with low cost.
But as mentioned above, the form of the Ti-Al-N ternary system ceramics of making of PVD method or CVD method is a film, about powder report as yet so far.
In the time that PVD method or CVD manufactured polynary system ceramic powder being used, produced the disadvantage that the matrix material manufacturing cost is increased sharply again.Its reason is: because the reaction efficiency of these methods is low and speed of response is slow, so the production efficiency of polynary system ceramic powder is low.Again, the reaction conditions that makes powder in these methods need be tried to achieve by experiment, therefore needs for a long time, and miscellaneous disadvantage displays.
As the additive method of making Ti-Al-N ternary system ceramics powder, remembered that the mixed powder with Ti and Al carries out nitrogenize.But, in this case, can only obtain the mixed powder of TiN and AlN, and can not obtain Ti-Al-N ternary system ceramics powder.
Therefore, expected the nitrogenize of Ti-Al two component system alloy.But the oxide film that its surface is formed by airborne oxygen institute's oxidation coats this alloy.Therefore make the nitrogenize of Ti-Al two component system alloy very difficult to inside, though with the powder that makes as raw material, do not find that the hardness of matrix material increases yet.
As mentioned above, make with two or more metallic elements and C or N and constitute the polynary system ceramic powder of element, therefore do not make this polynary system ceramic powder as yet with significant difficulty.
Summary of the invention
Main purpose of the present invention is to provide a kind of can making than the sintered compact that with the binary system ceramics is raw material to have more high rigidity and more the polynary system ceramic powder and the manufacture method thereof of the sintered compact of high tenacity, is the sintered compact and the manufacture method thereof of raw material with it.
According to a kind of example of the present invention, a kind of polynary system ceramic powder is provided, it is with the W of 56～92 weight %, 0.5 the Cr of～7 weight %, that chooses from Ti, Zr, Hf is at least a, that chooses from V, Nb, Ta is at least a, and the N of 0.3～8.2 weight % and C are constituent, and is below the 0.5 weight % as the ratio of the O that unavoidable impurities contained.
That is, a kind of form of polynary system ceramic powder of the present invention is, for example above carbonitride powder such as five yuan of systems shown in W-Cr-Ti-V-N-C or the W-Cr-Ti-Zr-V-Nb-N-C etc.
The sintered compact that is raw material with this polynary system ceramic powder demonstrates than higher hardness and the toughness of sintered compact that with binary system ceramics powder such as WC or NbC is raw material.Again, intensity, rigidity are basic identical.That is,, can improve hardness and toughness not damaging under intensity and the inflexible situation.
According to another example of the present invention, a kind of manufacture method of polynary system ceramic powder is provided, it comprises following operation: will be the material powder of constituent with W, with Cr is the material powder of constituent, with Ti, Zr or Hf are material powder at least a of constituent, with V, Nb or Ta are material powder at least a of constituent, for 100 weight % above-mentioned substances and with the ratio of 3.0～11.5 weight % powder carbon material that adds and the catalyst mix that promotes the carbon nitrogenize, by mechanically mixing generate with W and, Ti, Zr, at least a and the V of Hf, Nb, the operation of at least a powdered alloy for constituent of Ta and in the presence of nitrogen the mixed powder that contains above-mentioned powdered alloy heat-treated and make the nitrogenize of above-mentioned powdered alloy carbon becomes the operation of polynary system ceramic powder.
In manufacture method of the present invention, when implementing thermal treatment, at first will be present in the oxide film reduction on powdered alloy surface with the powder carbon material.Therefore, the surface of this powdered alloy becomes and has active state.Therefore, can be easy, easy and in large quantities from the surface to inside with this powdered alloy carbon nitrogenize.Therefore, can make the polynary system ceramic powder with low cost.The powder carbon material becomes CO or CO owing to making self oxidized the oxide film reduction
2These all are gas, therefore can be discharged to outside the Reaktionsofen easily and promptly.
According to another example of the present invention, a kind of sintered compact that contains the above polynary system pottery of 65 weight % is provided, this polynary system pottery is with the W of 56～92 weight %, 0.5 the Cr of～7 weight %, that chooses from Ti, Zr, Hf is at least a, that chooses from V, Nb, Ta is at least a, and the N of 0.3～8.2 weight % and C are constituent, and is below the 0.5 weight % as the ratio of the O that unavoidable impurities contained.
That is, the sintered compact among the present invention comprises only by above-mentioned five yuan of polynary system ceramic powder agglomerating sintered compacies more than the system and this polynary system ceramic powder and the mutual agglomerating matrix material of metal-powder.
This sintered compact demonstrates and be the essentially identical intensity of sintered compact and the rigidity of raw material with binary system ceramicss such as WC or NbC, again, demonstrates very high hardness and toughness.
According to another example of the present invention, providing a kind of serves as the manufacture method that constitutes the polynary system ceramic powder of element with at least two kinds of metallic elements and the N that choose from Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, W, it comprises following operation: will contain the powder compacting of the 1st material powder and become the molding procedure of formed body, wherein the 1st material powder with any of Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, W as constituting element; For with Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, among the W any and constitute the metallic element that do not contain in above-mentioned the 1st material powder of above-mentioned formed body above-mentioned formed body for the 2nd material contact that constitutes element, in the atmosphere that N exists, heat, when making metallic element as the formation element of above-mentioned the 2nd material be diffused in above-mentioned the 1st material, make the formation element and the N chemical combination of the 1st material, above-mentioned formed body is become by the metallic element that contains above-mentioned the 1st material, the metallic element of above-mentioned the 2nd material and N are as the heat treatment step of the porous sintered article of the polynary system pottery formation that constitutes element; By being pulverized, above-mentioned porous sintered article make above-mentioned polynary system pottery become the pulverizing process of powder.
That is, in this case, the polynary system ceramic powder of manufacturing is for two or more metallic elements and N serving as the polynary system pottery that constitutes more than the three component system of element.
In this manufacturing process, the metallic element that constitutes the 2nd material is diffused in the 1st material, and constitutes the metallic element and the N chemical combination of the 1st material this moment, thereby generates the above polynary system pottery of three component system.By with its pulverizing, can be easily and make the polynary system ceramic powder easily.
If constituting the metallic element of element as polynary system pottery is with a kind of, then compare with the sintered compact that with the nitride ceramics is raw material, be that the sintered compact of raw material demonstrates high rigidity with the carbonitride pottery.That is, preferred polynary system ceramic powder is also with the material of C as the formation element.In this case, the polynary system ceramic powder of manufacturing is for two or more metallic elements, N and C serving as the polynary system pottery that constitutes more than the quaternary system of element.
In order to make carbonitride (polynary system pottery) powder as the formation element, can in the presence of the powder carbon material, carry out above-mentioned heat treatment step with C.So just, produced the chemical combination of the metallic element of C and formation the 1st material.
According to another example of the present invention, provide that a kind of to contain with at least two kinds of metallic elements choosing and N be the manufacture method of polynary system ceramic sintered bodies that constitutes the polynary system pottery of element from Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, W, it comprises following operation: will contain the powder compacting of the 1st material powder and become the molding procedure of formed body, wherein the 1st material with any of Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, W as constituting element; For with Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, among the W any and constitute the metallic element that do not contain in above-mentioned the 1st material powder of above-mentioned formed body above-mentioned formed body for the 2nd material contact that constitutes element, in the atmosphere gas that N exists, heat, when making metallic element as the formation element of above-mentioned the 2nd material be diffused in above-mentioned the 1st material, make the formation element and the N chemical combination of the 1st material, above-mentioned formed body is become contain formation element with above-mentioned the 1st material, the formation element of above-mentioned the 2nd material and N are as the sintering circuit of the sintered compact of the polynary system pottery that constitutes element.
That is, in this case, by directly making the formed body sintering, make the sintered compact that contains the above polynary system pottery of three component system.
Even when making sintered compact, identical in the time of also can be with above-mentioned making powder, by in the presence of the powder carbon material, carrying out above-mentioned sintering circuit, can become carbonitride (polynary system pottery) sintered compact as the formation element with C.
Comparing with the sintered compact that with binary system ceramicss such as TiN, TiC, NbC or WC is raw material, should be that the sintered compact of raw material demonstrates high rigidity with the polynary system ceramic powder.Again, the relative density and the ideal density of this sintered compact are approaching, so this sintered compact also demonstrates high strength and high tenacity.
Description of drawings
Fig. 1 is the schema of the polynary system ceramic powder manufacture method of the 1st example.
Fig. 2 is the sintering pattern in the heat treatment step when making the polynary system ceramic powder of the 1st example.
Fig. 3 is for each becomes to be grouped into the chart with characteristic in the sintered compact of expression embodiment 1～28 and comparative example 1～4.
Fig. 4 represents to be the negative blade (negative tip) of principal constituent and to be that the negative blade of principal constituent is being cutting speed and life relation when being cut material with WC with the AC8B material with the polynary system ceramic powder.
Fig. 5 represents to be the negative blade of principal constituent and to be that the negative blade of principal constituent is being cutting speed and life relation when being cut material with WC with the FC250 material with the polynary system ceramic powder.
Fig. 6 represents with the polynary system ceramic powder, and to be the negative blade of principal constituent and negative blade that the surface forms hard layer respectively with the SCM435 material be cutting speed and life relation when being cut material.
Fig. 7 is the schema of the polynary system ceramic powder manufacture method of the 2nd example.
Fig. 8 is the schema of the polynary system ceramic sintered bodies manufacture method of the 2nd example.
Sintering pattern when Fig. 9 represents to make porous sintered article among the embodiment 29～31 in the heat treatment step.
Figure 10 represents along diametric distance that passes through in the porous sintered article bottom surface of embodiment 29～31 and Al concentration relationship.
Figure 11 is the sintering pattern of heat treatment step when making porous sintered article among the embodiment 32～34.
Figure 12 represents along the relation of the diametric distance that passes through in the porous sintered article bottom surface of embodiment 32～34 with A scale Rockwell hardness.
The optimal morphology that carries out an invention
Below enumerate suitable example and, polynary system ceramic powder of the present invention and manufacture method, sintered compact and manufacture method thereof are described in detail with reference to accompanying drawing.
At first, as the 1st example of the present invention,, use with the relation that with it is the sintered compact of raw material to describe for five yuan of polynary system ceramic powder and manufacture method thereof more than the system.
The sintered compact of the 1st example with W and Cr at least, from Ti, Zr, Hf, choose more than one, from V, Nb, Ta, choose more than one, N and the mutual chemical combination of C and carbonitride powder more than the hexa-atomic system that forms is a raw material.That is, this carbonitride serves as to constitute element with the metallic element more than four kinds, N and C.
W is the principal constituent of polynary system ceramic powder.As everyone knows, the nucleidic mass of W is big.Therefore given polynary system ceramic powder high specific gravity.With the high powder of proportion is that the sintered compact of raw material demonstrates high tensile strength and fatigue strength.Because powder is than great, therefore the sintering particle is difficult for vibration when the sintered compact stress application, so the stress wave propagation has obtained significant inhibition.From this viewpoint, the proportion of preferred polynary system ceramic powder is more than 10.Again, W is high rigidity, and the rigidity of sintered compact is improved.
The ratio of components of W is set at 56～92 weight % in the polynary system ceramic powder.If discontented 56 weight %, then the proportion of polynary system pottery reduces, consequently the insufficient strength of sintered compact.Again, the rigidity of sintered compact also descends.On the other hand, if surpass 92 weight %, then sintered compact hardness deficiency.
Cr improves the erosion resistance of polynary system ceramic powder and scale resistance.The raising of two characteristics particularly at high temperature can be confirmed significantly.Its reason be considered to be used to dissociate dissociation energy of key of Cr and C and N is big, therefore the chemical stability of polynary system ceramic powder is significantly improved.
Like this, because the scale resistance of sintered compact improves, for example,, be accompanied by electrodischarge machining(E.D.M.) and the thickness of the deterioration by oxidation layer that forms becomes minimum when using this sintered compact to carry out electrodischarge machining(E.D.M.) as mould and to this sintered compact.Usually, the deterioration by oxidation layer need be removed from sintered compact, but because thickness is minimum at this moment, can be easily with its removal.According to the difference of purposes, yet can the deterioration by oxidation layer not removed and use from sintered compact again.
The ratio of components of Cr is set at 0.5～7 weight % in the polynary system ceramic powder.If discontented 0.5 weight % then lacks the effect that erosion resistance or scale resistance are improved.Again, if surpass 7 weight %, then the rigidity of sintered compact or intensity reduce sometimes.
Ti, Zr or Hf form intermetallic compound (alloy) with W and Cr in very wide compositing range.On the other hand, Ti, Zr or Hf and N form chemically stable nitride.Therefore, for example nitrogenize easily such as W-Cr-Ti alloy.That is, Ti, Zr or Hf are used to make the N chemical combination easy composition that becomes.
The ratio of components that Ti, Zr or Hf suit in the polynary system ceramic powder is different.Particularly, when during as constituent, being 0.5～32 weight % only with Ti; When during as constituent, being 1～38 weight % only with Zr; When during as constituent, being 2～42 weight % only with Hf.If ratio of components is littler than above-mentioned value, then the ratio of components of N also diminishes in the polynary system ceramic powder, so the intensity of sintered compact and toughness are not enough.Again, if bigger than above-mentioned value, then the ratio of components of other elements such as W reduces relatively, therefore becomes hardness and the not enough sintered compact of rigidity.
When using Ti, Zr etc. two or more, can make ratio of components littler than above-mentioned value.For example, the ratio of components that can make Ti is 0.5 weight %, and the ratio of components that makes Zr is 0.5 weight %.In brief, when use is two or more, can be at the ratio of components that guarantee to set under sintered compact toughness, hardness and the inflexible situation them.
V, Nb or Ta make the hardness of sintered compact and the composition that toughness improves.That is, their solid solutions combine securely with both in two sides of W, Cr and Ti, Zr, Hf, and its result has given the sintered compact high rigidity.By their solid solution, the ratio of components of combinable N is increased again.Therefore the toughness of sintered compact improves.
The suitable ratio of components of V, Nb or Ta is different in the polynary system ceramic powder.That is, when during as constituent, being 0.5～11 weight % only with V; When during as constituent, being 1.2～20 weight % only with Nb; When during as constituent, being 2～39 weight % only with Ta.If ratio of components is littler than above-mentioned value, then the intensity of sintered compact and toughness reduce.If bigger, then become the not enough sintered compact of rigidity than above-mentioned value again.
Much less, when using V, Nb etc. two or more, can make the ratio of components of each element littler than above-mentioned value.For example, the ratio of components that can make V is 0.5 weight %, and the ratio of components that makes Nb is 1.0 weight %.In brief, in this case, when use is two or more, can be at the ratio of components that guarantee to set under sintered compact toughness, hardness and the inflexible situation them.
Again, except above-mentioned metallic element, preferably with the Al below the 3.0 weight % as constituent.When Al exists, as O and this Al chemical combination of inevitable impurity.Therefore, W and Ti, Zr, Hf, V, Nb, Ta oxidation are significantly suppressed, so the hardness of sintered compact, intensity, toughness and rigidity etc. further improve.If the ratio of components of Al surpasses 3.0 weight %, the hardness of sintered compact, intensity, toughness and rigidity all reduce.
N for to W and Cr, from Ti, Zr, Hf, choose at least a, that from V, Nb, Ta, choose at least a be that the nitrogen that is contained in the powdered alloy of the constituent atmosphere when heat-treating serves as that the source is supplied with.As described later, in the presence of powder carbon material and nitrogen,, make polynary system carbonitride ceramic powder by above-mentioned alloy is heated.
The ratio of components of N is set at 0.3～8.2 weight %.If the ratio of components of N is not in this scope, then the hardness of sintered compact reduces.
As mentioned above, C for the powder carbon material serve as the source supply with.To contain C is that the polynary system ceramic powder of constituent is a raw material, can make the sintered compact of high rigidity.
Again, this polynary system ceramic powder contains the O as unavoidable impurities.The ratio of this O is set at below the 0.5 weight %.Reason is that the hardness of sintered compact and intensity reduce if surpass 0.5 weight %.
As the sintered compact of the 1st example, enumerate the material that for example only above-mentioned polynary system ceramic powder sintering is obtained.It is the sintered compact of raw material that the hardness of this sintered compact, intensity and rigidity significantly are better than with binary system ceramics powder such as WC.Particularly, be about 1800 to compare with WC sintered compact Vickers' hardness, the formed sintered compact of W-Cr-Ti-Zr-Nb-Al-C-N ceramic powder sintering demonstrates the hardness more than 2800.
Again, the sintered compact of the 1st example matrix material that can obtain with the metal-powder sintering for the polynary system ceramic powder.As metal-powder, for example can choose general Fe, Ni as the raw material of composite mould or composite cutting tool, Co or at least a alloy for constituent etc. in them.In this case, be that the matrix material of same ratio of components is compared with pottery and metal, demonstrate hardness, intensity and the rigidity of remarkable excellence.
During for matrix material, the ratio of components of polynary system pottery is set at more than the 65 weight % in the sintered compact.If be lower than 65 weight %, because the ratio of components of pottery reduces relatively, so reductions such as the hardness of sintered compact, intensity, rigidity.
Polynary system ceramic powder as the sintered compact raw material can as described belowly be made.
The schema of the polynary system ceramic powder manufacture method of this example as shown in Figure 1.The acid treatment operation S3 that the polynary system ceramic powder that this manufacture method comprises the heat treatment step S2 that heat-treats with the mechanically mixing operation S1 of raw material powder, powder carbon material, catalyst mix, to the mixed powder that makes, make thermal treatment with acid solution is handled.
At first, in mechanically mixing operation S1, with raw material powder, powder carbon material and catalyst mix.
To choose with W be the material powder of constituent, with Cr be constituent material powder, at least a with Ti, Zr or Hf be constituent material powder and at least a be that the material powder of constituent is as raw material powder with V, Nb or Ta.That is, raw material powder contains W source and Cr source, at least a and V source, Nb source or the Ta source in Ti source, Zr source or Hf source at least a.
The W source can be W self, and promptly the W powder also can be the powder of W compound.Equally, other metallic element sources can be the powder of pure metal, also can be the powder of compound.Compound is easy oxidation or reductive material in heat treatment step S2 preferably.This material comprises for example hydride such as titanium hydride or Vanadium hydride.
The W in the W source of containing in the raw material powder and the Cr in Cr source, the Zr in the Ti in Ti source, Zr source or the Hf's in Hf source is at least a, and the Nb in the V in V source, Nb source or the Ta's in Ta source is at least a, generates alloy easily by mechanically mixing.
When being polynary system pottery constituent with Al, can also add with Al in the above-mentioned raw materials powder is the material of constituent, promptly becomes the material in Al source.As the Al source, it comprises for example Al powder.The adding proportion in Al source is below the 3 weight %.If add manyly than 3 weight %, because the ratio of components of Al surpasses 3 weight % in the polynary system pottery, hardness, intensity, toughness and the rigidity of sintered compact all reduce as a result for they.
The powder carbon material plays the effect in polynary system pottery C source.On the other hand, the powder carbon material reduces the oxide film that above-mentioned W source, Cr source, Ti source, Zr source, Hf source, V source, Nb source, Ta source, surface, Al source form.That is, usually, these metals so that the surface of hydride etc. because by the oxidation of airborne oxygen institute, therefore the oxide film that is formed covers.When heat-treating operation S2, because self is oxidized, so the powder carbon material is with this oxide film reduction.
Here, the adding proportion of powder carbon material is set in the scope of 0.1 weight %～11.6 weight %.If less than 0.1 weight %, then the ability as reductive agent lacks.If surpass 11.6 weight %, then generate uncombined carbon again.In addition, when adding the Al powder, also generate Al
4C
3The sintered compact that contains this material is not enough aspect hardness and toughness.
Catalyzer is used to promote with above-mentioned metallic element to be the carbon nitrogenize of the alloy of constituent.The preference of catalyzer comprises alkaline-earth metal, VIIA family element, group VIII element.Wherein, preferably use VIIA family element or group VIII element.These materials are easy to stripping in acid solution in acid treatment operation S3 described later, therefore can obtain highly purified polynary system ceramic powder.The group VIII element for example comprises Fe, Co, Ni, and VIIA family element for example comprises Mn.Wherein, owing to promote that the effect of above-mentioned nitride metal or carbon nitrogenize is the most excellent, the therefore preferred Mn that uses.
Preferred catalyzer adding proportion cannot treat different things as the same because of the difference of catalyst type is different.For example, when using Mn below the preferred 3 weight %, when using Fe, Co, Ni below the preferred 5 weight %.Add catalyzer if surpass aforementioned proportion, under any circumstance, the growing amount of the residual quantity of unreacted catalyzer or their nitride or carbonitride increases.Therefore, owing in acid treatment operation S3, be difficult for, therefore be difficult to make the hardness of sintered compact to improve with these material strippings.
As catalyzer, it not only can be the pure substance of alkaline-earth metal, VIIA family element or group VIII element, also can use compound.For example, can replace the powder of Fe, Ni and use the powder of iron carbonyl, nickle carbonoxide.Compare with the pure substance powder, the particle diameter of these compound powders significantly reduces.Therefore, owing to be distributed in the mixed powder equably, therefore can promote nitrogenize or carbon nitrogenize with the addition that lacks than the pure substance powder.Therefore, can save resource, favourable aspect cost.
Again, catalyzer also can be the two or more elements the chosen alloy as constituent from alkaline-earth metal, VIIA family element, group VIII element.This material comprises for example Mg-Ni, Ca-Co, Mg-Fe etc.
Make W and Cr with mechanically mixing, at least a among Ti, Zr, the Hf, under the condition of at least a generation alloy, carry out the mixing of above raw material powder, powder carbon material and catalyzer among V, Nb, the Ta.Particularly, raw material powder, powder carbon material, catalyzer and steel ball packed into to be constituted in the water-cooled vessel of vertical ball mill, with this water-cooled vessel sealing, makes the rotation oar rotation of inserting in this water-cooled vessel.Like this, friction and crimping between the metal-powder under high-energy, its result generates powdered alloy.Again, reductive agent and catalyzer roughly are dispersed in the powdered alloy equably.
Then, in heat treatment step S2, in the presence of nitrogen, the above-mentioned mixed powder that contains powdered alloy that makes is heat-treated.Nitrogen can be contained in the atmosphere gas that can make the nitrogenize of powdered alloy carbon.That is, can be only with nitrogen as atmosphere gas, also can with nitrogen and other rare gas elementes for example the mixed gas of argon gas etc. as atmosphere gas.
Again, heat treated temperature is preferably 1000 ℃～1600 ℃.If be lower than 1000 ℃, can not carry out the carbon nitrogenize effectively.Again, even surpass 1600 ℃, the speed of carrying out of carbon nitrogenize also no longer improves, so the manufacturing cost of polynary system pottery increases.
In heat treatment step S2, the at first oxide film reduction that the powdered alloy surface is formed.That is, the surperficial oxide film of powdered alloy coats, and the metal that this oxide film constitutes this powdered alloy is formed by airborne oxygen oxidation.This oxide film is reduced by the powder carbon material, becomes active powdered alloy.
When carrying out this reduction, the powder carbon material makes autoxidation by capturing oxygen from oxide film, becomes CO or CO
2Because they are gas, therefore can accompany with the atmosphere gas phase, also promptly be discharged to outside the Reaktionsofen easily.That is, there is not oxide compound residual.Therefore, can make highly purified polynary system ceramic powder.
Because oxide film is reduced, the surface of powdered alloy is in extremely active state.Therefore, when the remaining powder carbon material played a role with the C source, the N that is contained in the atmosphere gas played the effect in N source, consequently powdered alloy from the surface to inside all by the carbon nitrogenize.
When heat-treating operation S2, catalyzer is also oxidized sometimes.That is,,, be mixed with the oxide compound of unreacted catalyzer and catalyzer by in the resulting polynary system ceramic powder of heat treatment step S2 as impurity.When with the polynary system ceramic powder that is mixed with these impurity being raw material manufacturing sintered compact, this sintered compact shows soft sometimes.
Therefore, preferably in acid treatment operation S3 subsequently, impurity separated from the polynary system ceramic powder and remove.Particularly, impregnated in the acid solution by the polynary system ceramic powder that will make, thereby with the impurity stripping.
Preferably, in this acid solution, contain hydrofluoric acid or fluorine boron hydracid.Its reason is: because they have excellent dissolving power to above-mentioned impurity, therefore can effectively impurity be separated from the polynary system ceramic powder and remove.
At this moment, coming from different backgrounds and possess different abilities is that the part of metallic element of ceramic powder is also oxidized sometimes.As mentioned above, the powder that surpasses 0.5 weight % with the ratio of O is the sintered compact of raw material, and its hardness reduces.Therefore, the concentration of setting acid solution or dipping time are so that the ratio of O is no more than 0.5 weight %.
Filter after liquid and the powder separation, powder is carried out neutralizing treatment and washing, thereby make highly purified polynary system ceramic powder.
Because all by nitrogenize or carbon nitrogenize, therefore the sintered compact that is raw material with this polynary system ceramic powder demonstrates high rigidity to this polynary system ceramic powder from the surface to inside.Again, because impurity is removed from the polynary system ceramic powder, so the relative density of sintered compact is near theoretical density.Therefore, this sintered compact has excellent intensity and toughness.
Like this, with W source and Cr source, at least a in Ti source, Zr source or the Hf source, V source, Nb source or Ta source at least a, and after Al source in case of necessity and powder carbon material, the catalyst mix, in the presence of nitrogen, heat-treat, can be easily and make the polynary system ceramic powder easily.And in this manufacture method, compare its reaction efficiency height and speed of response height with PVD method or CVD method.Therefore, the turnout of each batch is many, thereby can make the cheap for manufacturing cost of sintered compact.
The purposes of sintered compact for example comprises that machining such as blade or lathe tool are with cutlery or mould etc.
1. the characteristic of sintered compact
With W powder and Cr powder, titanium hydride powders, zircoium hydride powder or Hf powder at least a, changing vanadium powder end, Nb powder or at least a of Ta powder be raw material powder, to the above-mentioned substance of 100 weight %, with the ratio interpolation carbon black of 3.0～11.5 weight %.In raw material powder, add 3 weight % in case of necessity with interior Al.And then add Mg, Mn, Ni as catalyzer, be mixed together with raw material powder.Make W and Cr with mechanically mixing, at least a among Ti, Zr, the Hf, at least a among V, Nb, the Ta (when adding Al, also comprising Al) generates under the condition of alloy, carries out this mixing.
Under nitrogen atmosphere, heat-treat by form shown in Figure 2, make the powdered alloy carbon nitrogenize in the above-mentioned mixed powder that makes, thereby make various polynary system ceramic powder.
And then, this polynary system ceramic powder be impregnated in the mixing solutions of chloroazotic acid or hydrofluoric acid and nitric acid, make unreacted Mg, Mn, Ni or their oxide compound stripping in acid solution, thus refining.This polynary system ceramic powder sintering after becoming sintered compact, is being measured the Vickers' hardness of each sintered compact.These are designated as embodiment 1～28, comparative example 1～4 respectively.
Ratio of components, Vickers' hardness (Hv) and the Young's modulus of elasticity of each constituent in each sintered compact of embodiment 1～28, comparative example 1～4 are shown in Fig. 3 in the lump.The value of Young's modulus of elasticity is big more, represents that more it is high rigidity.As seen from Figure 3, each sintered compact of embodiment 1～28 demonstrates very high hardness and rigidity, and when the ratio of components of W during less than 62 weight %, the hardness of sintered compact reduces.Again, by adding Al, the hardness of sintered compact improves.
After the powder of embodiment 26 and Co powder mixed, this mixed powder is sintered into composite sinter (below be called embodiment sintered compact 1,2) with 90: 10 (weight ratio, down with) or 93: 7 again.On the other hand, in order to compare, WC powder and Co powder were mixed with 90: 10, with mixed powder and WC powder, TaC powder, NbC powder and Co powder with 90: 1: 2: 7 mix, and make composite sinter (below be called comparative example sintered compact 1,2) respectively by the mixed powder that makes.Then to each complex sintered body measurement Vickers' hardness, folding strength and destruction toughness value.
Particularly, composite sinter is cut off at central section, section is carried out the minute surface aftertreatment after, measure the Vickers' hardness of this section, embodiment sintered compact 1 is 2400～2500, embodiment sintered compact 2 is 2400～3000.In contrast to this, comparative example sintered compact 1 is 1300～1340, and comparative example sintered compact 2 is 1550～1580, and is all little than embodiment sintered compact 1,2.
Again, cut out the test film of JIS folding strength regulation method defined from composite sinter, measure folding strength, embodiment sintered compact 1,2 is respectively 2.9GPa, 2.4GPa; Comparative example sintered compact 1,2 is respectively 2.8GPa, 2.2GPa, and folding strength also is embodiment sintered compact 1,2 excellences.
Again, measure the destruction toughness value according to the IF method, embodiment sintered compact 1,2 is respectively 20MPam
1/2, 13MPam
1/2Comparative example sintered compact 1,2 demonstrates very little value, is respectively 14MPam
1/2, 7MPam
1/2
Can see from above result, be raw material with the polynary system ceramic powder, under the situation of not damaging intensity, can make the sintered compact of high rigidity and high tenacity.
In addition, Young's modulus of elasticity is measured, embodiment sintered compact 1,2 is respectively 540GPa, 510GPa; Comparative example sintered compact 1,2 is respectively 570GPa, 610GPa, and comparative example sintered compact 1,2 demonstrates slightly high value.But when embodiment sintered compact 1,2 was used as processing with cutlery or mould, the Young's modulus of elasticity (rigidity) of embodiment sintered compact 1,2 was enough values.
2. as the cutting power of cutting with cutlery
With the polynary system ceramic powder of embodiment 26 and TaC powder, NbC powder, Co powder with 91: 1: 1: after 7 ratio is mixed, carry out sintering, making inscribed circle is that 12.7mm and thickness are the negative blade of embodiment of 4.76mm.For relatively, use the WC powder except replacing the polynary system ceramic powder, similarly make the negative blade 1 of comparative example of same size.
Then with each negative blade, for AC8B material (silumin material) or FC250 material (cast iron materials), carry out the various variations of cutting speed with the 0.26mm/ commentaries on classics, form the hole that the degree of depth is 2mm continuously, the relation between the time when investigation cutting speed and abrasion amount reach 0.3mm.The result is shown in Fig. 4, Fig. 5 respectively.From these figure, can see antifriction consumption, long lifetime that negative blade one side of embodiment has remarkable excellence.
Again, for the negative blade 1 of comparative example, along with the carrying out of processing, form structure sword end, consequently the dimensional precision in hole also reduces.In contrast to this, for the negative blade of embodiment, in the process of processing, do not find the formation of structure sword end, the hole precision height of setting.
Again, negative blade 2 of preparation comparative example and the negative blade 3 (being commercially available product) of comparative example, wherein the negative blade 2 of comparative example is TiN, Al
2O
3, TiC, TiCN, TiN totally 5 layers form on the suitable material surface of JISP10 by this order, the negative blade 3 of comparative example is to be formed on the surface of the suitable material of JIS P10 by the layer that the Ti-Al-N ternary nitride constitutes.For Rockwell hardness is that 48 SCM435 material (steel) is provided with the cutting test that diameter is the 2mm hole continuously, investigates and escapes in the face of the long abrasion amount of cutting.Machining condition is: cutting speed 230mm/ branch, transfer rate 0.26mm/ change.The negative blade of result and the foregoing description is shown in Fig. 6 in the lump.
As seen from Figure 6, for the negative blade of embodiment, whether tube-surface does not form hard layer, and the abrasion amount is lacked than the negative blade 2,3 of comparative example, and promptly antifriction consumption excellence has the long lifetime.Its reason is that the negative blade of embodiment is starting material with the big polynary system carbonitride pottery of dissociation energy.
Below, to as the 2nd example of the present invention, serve as to constitute the nitride ceramics of element or serve as that the manufacture method that constitutes the carbonitride ceramic powder of element, the manufacture method that contains the sintered compact of above-mentioned nitride ceramics or above-mentioned carbonitride pottery describe with metallic elements two or more at least in the above-mentioned substance and N, C with the two or more at least metallic elements from Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, W, chosen and N.
As mentioned above, in the 2nd example, it is not serving as different with the 1st example on the necessary composition this point with W and Cr.
With reference to its schema Fig. 7 the manufacture method of the polynary system ceramic powder of the 2nd example is described.The method for making of this powder comprise the shaping raw material powder and form formed body molding procedure S10, make above-mentioned formed body become the heat treatment step S20 of the porous sintered article that constitutes by the polynary system pottery and the pulverizing process S30 that above-mentioned porous sintered article is pulverized.
At first in molding procedure S10, make the formed body that constitutes by the 1st material.
As the selected raw material powder of formed body starting material, if its be with Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, W any is the material powder of formation element at least, both can be pure metal, also can be alloy or compound.For example, as being the material that constitutes element with Ti, can use Ti powder, TiC powder, TiN powder, Ti (C, N) powder, TiO
2Powder, organic Ti compound powder etc.; As being the material that constitutes element with W, can use W powder, W-Ti powdered alloy, W
2O
3Powder, WC powder etc.Owing to can especially easily make the polynary system ceramic powder, therefore preferred nitride, carbide, carbonitride.
Raw material powder can be the powder of single kind, also can be for example mixed powder of the two or more powder mixes such as mixed powder of WC powder, TiC powder and NbC powder.That is, the 1st material can be made of single kind, also can be made of mixture.
Here, preferably in the 1st material, add the catalyzer that promotes nitrogenize or carbon nitrogenize.The preference of catalyzer comprises alkaline-earth metal, VIIA family element or group VIII element.VIIA family element comprises for example Mn, and the group VIII element comprises for example Fe, Co, Ni.Wherein, owing to promote that the effect of above-mentioned nitride metal or carbon nitrogenize is the most excellent, the therefore preferred Mn that uses.
The preferred adding proportion of catalyzer cannot treat different things as the same because of the difference of catalyst type is different.For example, when using Mn below the preferred 3 weight %, when using Fe, Co, Ni below the preferred 5 weight %.Add catalyzer if surpass aforementioned proportion, under any circumstance, the growing amount of the residual quantity of unreacted catalyzer or the nitride of this catalyzer or carbonitride increases, and therefore is difficult to make the hardness of sintered compact to improve.
As catalyzer, it not only can be the pure substance of alkaline-earth metal, VIIA family element or group VIII element, also can use compound.For example, can replace the powder of Fe, Ni and use the powder of iron carbonyl, nickle carbonoxide.Compare with the pure substance powder, the particle diameter of these compound powders significantly reduces.Therefore, owing to be distributed in the mixed powder equably, can promote nitrogenize or carbon nitrogenize with the addition that lacks than the pure substance powder.Therefore, can save resource, favourable aspect cost.
The powder for preparing the 1st material as mentioned above, so in this powder, add resin, paraffin and wax etc. as tackiness agent after, with moulding such as moulded section methods, thereby make formed body.
Perhaps, also can be after in powder, adding the ethanol equal solvent, mixed powder and solvent be filled into together be provided with in the aisled mould die cavity, under this state, mixed powder and solvent are pressurizeed with this mould.In this case, after the pressurization, solvent is at first mobile, thereby separates with mixed powder, between this mixed powder and mould.Its result is because mixed powder by the extruding of solvent approximate equality ground, has therefore significantly suppressed by producing crack or defective in the mixed powder making formed body.That is, in this forming method, at first mixed powder has been carried out the isotactic pressing that solvent produces.
Along with the carrying out of pressurization, solvent is discharged to outside the die cavity by the above-mentioned path that is provided with in the mould.Therefore, mixed powder is directly pushed by mould subsequently.Like this, because solvent is discharged, therefore do not hinder and use mould that mixed powder is pressurizeed.
At this moment, needn't in powder, add resin, paraffin and wax etc.Therefore, degreasing process can be omitted, thereby the polynary system ceramic powder can be made efficiently.
In heat treatment step S20, make the above-mentioned formed body that makes become porous sintered article.That is, make it leave pore.
At this moment, for example use the parts that constitute by the 2nd material that the surface of formed body is centered on, thereby the 2nd material is contacted with formed body.Or also can be on the parts that the 2nd material constitutes with the formed body mounting.Again, also can be with the 2nd material powder coated to the surface of formed body.
As the 2nd material, choose with the metallic element that do not contain in the 1st material as the material that constitutes element.Particularly, when material that formed body (the 1st material) makes for the mixed powder moulding of WC powder and TiC powder, the 2nd material does not serve as to constitute element with W or Ti, can select for example Al or Al alloy etc., at the surface coated Al or the Al powdered alloy of formed body.Perhaps, the component configuration that also Al or Al alloy can be constituted is in the outside of formed body.
Here, when the 2nd material is the material of the easy formation in the surface oxide film as Al or Al alloy etc., preferably use reductive agent with this oxide film reduction.The preferred powder carbon material of reductive agent.In this case, the C that is the source with this powder carbon material also becomes the formation element of polynary system pottery.
The powder carbon material can be mixed in the powder of Al or Al alloy, is applied to the surface of formed body.Or, also can add in advance in the powder of the 1st material, make it become formed body.
Under this state, the 1st material powder that constitutes formed body does not carry out densification (sintering), and under the temperature in formation Elements Diffusion to the 1 material of the 2nd material formed body is carried out heat treated.If above-mentioned example can be set at Heating temperature about 1100K.
This heat treated is carried out in the atmosphere that N exists.Particularly, can make atmosphere gas is N
2Or NH
3, or both mixed gass.In addition, also can there be rare gas elementes such as Ar.Owing to handle easily the therefore preferred N that uses
2Or N
2Mixed gas with rare gas element.
In these cases, by this heat treated, at first the oxide film that forms on Al (the 2nd material) surface is reduced, and this surface exposes active Al.Therefore, Al can easily spread.
That is, in heat treatment step S20, be active Al when in WC or TiC, spreading, WC or TiC and N chemical combination.Its result generates the quaternary system carbonitride pottery shown in W-Al-C-N, the Ti-Al-C-N.Again, because the reaction of the part of WC and TiC, generating five yuan of W-Ti-Al-C-N sometimes is the carbonitride pottery.As a result, in above-mentioned porous sintered article, contain above-mentioned polynary system pottery.
When using the powder carbon material as reductive agent, thus this powder carbon material capture oxygen from oxide film and make self oxidized, form CO or CO
2Because these materials are gas, therefore can follow the atmosphere air-capacitor easily and promptly to be discharged to outside the Reaktionsofen.
Again, the remaining powder carbon material also plays the effect in C source.That is, when the 1st material is the powder of the powder of pure metal or nitride, be C and these material chemical combination in source, so also produce carbonization nitrogenize the time with the powder carbon material.
At last, in pulverizing process S30,, therefore obtain the polynary system ceramic powder because this porous sintered article is pulverized.When in the powder that is making during the residual powder that unreacted the 1st material arranged, can be with the powder separation of currently known methodss such as precipitate and separate with polynary system ceramic powder and the 1st material.
The polynary system ceramic powder that makes can be used as the suitable raw material use with cutlery or mould etc. such as the machining that is applicable to blade or lathe tool.That is, separately or after the metal-powder moulding, make this polynary system ceramic powder sintering, the machining that can make high rigidity is with cutlery or mould etc.
Following with reference to its schema Fig. 8, describe with regard to the manufacture method of the polynary system ceramic sintered bodies of the 2nd example.The method for making of this sintered compact comprises thereby the raw material powder moulding is become the molding procedure S100 of formed body, thereby this formed body sintering become the sintering circuit S200 of sintered compact.
At first, carry out molding procedure S100.Because this molding procedure S100 can carry out according to the molding procedure S10 of the polynary system ceramic powder method for making of above-mentioned the 2nd example, therefore omit its detailed description.In the time will making the matrix material of polynary system pottery and metal, further mixing in the powder of the 1st material with Fe, Co, Ni or in them more than one serves as that the powdered alloy of formation element gets final product.
Then, in sintering circuit S200 with the formed body sintering.Except making Heating temperature is can make the 1st material powder agglomerating temperature that constitutes formed body, can carry out this sintering circuit S200 according to the heat treatment step S20 of above-mentioned powder method for making.
That is, the parts that constitute with the 2nd material center on formed body, or with the powder coated surface to formed body of the 2nd material, thereby formed body is contacted with the 2nd material.Much less, even in the method for making of sintered compact, the also selected metallic element that does not contain with the 1st material serves as to constitute the material of element as the 2nd material.Again, identical with the method for making of powder, also can and use reductive agent.
Under this state, under the 1st material powder agglomerating temperature that causes the formation formed body, this formed body is carried out heat treated.Causing under the agglomerating temperature that the formation element of the 2nd material easily is diffused in the 1st material.For example, when formed body contained WC powder and TiC powder and the 2nd material and is Al, can make Heating temperature was about 1700K.Identical with the method for making of above-mentioned powder, in the atmosphere that N exists, carry out this sintering circuit S200.
In these cases, by this sintering, Al when in WC or TiC, spreading, WC or TiC and N chemical combination.Its result generates quaternary system carbonitride potteries such as containing W-Al-C-N, Ti-Al-C-N or W-Ti-Al-C-N is the sintered compact of carbonitride pottery for five yuan.Mixed metal powder in the powder of the 1st material and when becoming formed body, this sintered compact becomes the matrix material of polynary system pottery and metal.
As mentioned above, according to the sintered compact method for making of the 2nd example, by being shaped to the formed body sintering with the corresponding shape of purposes in advance, can be easily and make sintered compact easily with desired shape.
3. the preparation method of powder of the 2nd example
With ethanol is solvent, and the WC powder of 85.5 weight part median sizes, 1 μ m, the TiC powder of 15 weight part median sizes, 1.5 μ m, the carbonyl nickel powder of 1 weight part median size, 0.2 μ m, the Mg powder of 0.5 weight part are carried out wet mixing.Then, solvent is modulated to 3 weight parts after, this mixed powder be filled into solvent be provided with in the aisled mould die cavity.Do not add tackiness agent.
Then, by the above-mentioned path that in mould be provided with ethanol be discharged to die cavity outside on one side, with 120MPa mixed powder is pressurizeed on one side, make the cylindric formed body of 3 diameter 40mm * long 60mm.
Then, with the mixed powder that 1: 3 weight ratio mixes, make thickness reach 1mm at the carbon black of the surface coated Al of 1 cylindric formed body powder and median size 0.4 μ m.With it as embodiment 29.Again, in surface coated the side surrounding wall portion of another cylindric formed body of sooty connect airtight the cartridge that constitutes by the suitable material of JIS 1N99 (Al alloy).With it as embodiment 30.And, on a bottom surface of the diameter 50mm * 10mm disc that constitutes by the suitable material of JIS 1N99 the mounting surface coated another cylindric formed body of sooty.With it as embodiment 31.
Then, at N
2In the atmosphere, respectively these the cylindric formed bodys among the embodiment 29～31 are heat-treated, make it become porous sintered article according to heating mode shown in Figure 9.In all cases, under reduced pressure heat up, make N after this until arriving 950K
2Press and be 0.1MPa.
With Resins, epoxy with the lining of these porous sintered articles after, cut off along the bottom surface diametric(al), grind then, become electron microscope observation with and X-ray diffraction mensuration sample.
Figure 10 represents the relation of the concentration of the diametric distance that passes through and Al along each porous sintered article bottom surface.Can see that from this Figure 10 in embodiment 29～31, Al is diffusion equably roughly.
In X-ray diffraction is measured, find to have unknown peak to occur.This unknown peak is belonged to the polynary system pottery by supposition.This shows,, obtained the polynary system ceramic powder by these porous sintered articles are pulverized.In X-ray diffraction was measured, the Al peak did not appear.
4. the manufacture method of the sintered compact of the 2nd example
With ethanol is solvent, and the WC powder of 72.6 weight part median sizes, 1 μ m, the TiC powder of 15 weight part median sizes, 1.5 μ m, the NbC powder of 3 weight part median sizes, 1.5 μ m, the TaC powder of 2 weight part median sizes, 1.5 μ m, the Co powder of 7 weight part median sizes, 1.2 μ m, the carbonyl nickel powder of 0.2 weight part median size, 0.2 μ m are carried out wet mixing.Then, solvent is modulated to 3 weight parts after, this mixed powder be filled into solvent be provided with in the aisled mould die cavity.Do not add tackiness agent this moment yet.
Then, by the above-mentioned path that in mould be provided with ethanol be discharged to die cavity outside on one side, with 120MPa mixed powder is pressurizeed on one side, make the cylindric formed body of 3 diameter 40mm * long 80mm.
Below with embodiment 29～31 identical preparation samples.That is, with the mixed powder that 1: 3 weight ratio mixes, make thickness reach 1mm at the carbon black of the surface coated Al of 1 cylindric formed body powder and median size 0.4 μ m.With it as embodiment 32.Again, in surface coated the side surrounding wall portion of another cylindric formed body of sooty connect airtight the cartridge that constitutes by the suitable material of JIS 1N99 (Al alloy).With it as embodiment 33.And, on a bottom surface of the diameter 50mm * 10mm disc that constitutes by the suitable material of JIS 1N99 the mounting surface coated another cylindric formed body of sooty.With it as embodiment 34.
At N
2In the atmosphere, respectively these the cylindric formed bodys among the embodiment 32～34 are heat-treated, make it be sintered into sintered compact according to heating mode shown in Figure 11.In embodiment 32～34, under reduced pressure heat up until arriving 950K, make N after this
2Press and be 0.1MPa.
Along the diametric(al) of bottom surface these sintered compacies are cut off, after further grinding, pass through along diametric(al) and to measure near the Rockwell hardness (H of the A scale bottom surface
RA).The results are shown in Figure 12.Can see that from this Figure 12 the hardness ratio WC sintered compact or the TiC sintered compact of the sintered compact of embodiment 32～34 are much higher.
These sintered compacies are carried out X-ray diffraction measure, unknown peak occurring with the roughly same angle of embodiment 29～31 place.This has also supported to generate the conclusion of polynary system pottery.
Confirm that further almost do not have remaining pore in each sintered compact, relative density is roughly 100%.
Claims (11)
1, a kind of serves as the manufacture method that constitutes the polynary system ceramic powder of element with at least two kinds of metallic elements and the N that choose from Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, W, it is characterized in that, comprise: will contain the powder compacting of the 1st material powder and become the molding procedure of formed body, wherein the 1st material with any of Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, W as constituting element; For with Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, the metallic element that does not contain in any and above-mentioned the 1st material powder among the W is the above-mentioned formed body of the 2nd material contact that constitutes element, in the atmosphere that N exists, heat, when making metallic element as the formation element of above-mentioned the 2nd material be diffused in above-mentioned the 1st material, make the formation element and the N chemical combination of the 1st material, thereby above-mentioned formed body is become by the metallic element that contains above-mentioned the 1st material, the metallic element of above-mentioned the 2nd material and N are as the heat treatment step of the porous sintered article of the polynary system pottery that constitutes element; By being pulverized, above-mentioned porous sintered article make above-mentioned polynary system pottery become the pulverizing process of powder.
2, the manufacture method of claim 1 record is characterized in that, above-mentioned heat treatment step is included in the powder carbon material and has the above-mentioned formed body of heating down, thereby makes the formation element bonded operation of C and above-mentioned polynary system pottery.
3, the manufacture method of claim 1 or 2 records is characterized in that above-mentioned the 1st material comprises carbide, nitride or carbonitride.
4, the manufacture method of each record in the claim 1～3 is characterized in that, also is included in the operation of mixing the catalyzer that promotes nitrogenize or carbon nitrogenize in the powder of above-mentioned the 1st material.
5, the manufacture method of claim 4 record is characterized in that, above-mentioned catalyzer comprises that with alkaline-earth metal, VIIA family element or group VIII element be the material that constitutes element.
It is 6, a kind of that to contain with at least two kinds of metallic elements choosing among Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, the W and N be the manufacture method of sintered compact that constitutes the polynary system pottery of element, it is characterized in that, comprise: will contain the powder compacting of the 1st material powder and become the molding procedure of formed body, wherein the 1st material with any of Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, W as constituting element; For with Ti, Al, V, Nb, Zr, Hf, Mo, Ta, Cr, the metallic element that does not contain in any and above-mentioned the 1st material powder among the W is the above-mentioned formed body of the 2nd material contact that constitutes element, in the atmosphere that N exists, heat, when making metallic element as the formation element of above-mentioned the 2nd material be diffused in above-mentioned the 1st material, make the formation element and the N chemical combination of the 1st material, thereby above-mentioned formed body is become contain formation element with above-mentioned the 1st material, the formation element of above-mentioned the 2nd material and N are as the sintering circuit of the sintered compact of the polynary system pottery that constitutes element.
7, the manufacture method of claim 6 record is characterized in that, above-mentioned sintering circuit is included in the powder carbon material and has the above-mentioned formed body of heating down, thereby makes the formation element bonded operation of C and above-mentioned polynary system pottery.
8, the manufacture method of claim 6 or 7 records is characterized in that above-mentioned the 1st material comprises carbide, nitride or carbonitride.
9, the manufacture method of each record in the claim 6～8, it is characterized in that, also be included in and make Fe, Co, Ni before above-mentioned powder of moulding and the above-mentioned formed body of sintering or with more than one the operations in them as the powder mixes of the powder of the alloy that constitutes element and above-mentioned the 1st material.
10, the manufacture method of each record of claim 6～9 is characterized in that, also is included in the operation of mixing the catalyzer that promotes nitrogenize or carbon nitrogenize in the powder of above-mentioned the 1st material.
11, the manufacture method of claim 10 record is characterized in that, above-mentioned catalyzer comprises that with alkaline-earth metal, VIIA family element or group VIII element be the material that constitutes element.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001202139A JP4105410B2 (en) | 2001-07-03 | 2001-07-03 | Multi-component carbonitride powder, method for producing the same, and sintered body using the same |
| JP2001202198 | 2001-07-03 | ||
| JP2001202139 | 2001-07-03 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB028132939A Division CN100422362C (en) | 2001-07-03 | 2002-06-27 | Multi-element ceramic powder and method for preparation thereof, and sintered compact and method for preparation thereof |
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| CN1724469A true CN1724469A (en) | 2006-01-25 |
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ID=19038996
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|---|---|---|---|
| CN 200510087663 Pending CN1724469A (en) | 2001-07-03 | 2002-06-27 | Method for manufacturing multi-element ceramic powder and sintered compact |
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| JP (1) | JP4105410B2 (en) |
| CN (1) | CN1724469A (en) |
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| CN101255060B (en) * | 2008-03-26 | 2010-09-08 | 重庆大学 | Method for preparing diffusion couple by using powder |
| CN103975414A (en) * | 2012-07-03 | 2014-08-06 | 株式会社东芝 | Tungsten alloy part, and discharge lamp, transmitting tube and magnetron using same |
| CN105970065A (en) * | 2016-05-31 | 2016-09-28 | 合肥正浩机械科技有限公司 | Cubic boron nitride-carbonyl nickel powder metal ceramic sealing ring and preparation method thereof |
| WO2019095715A1 (en) * | 2017-11-15 | 2019-05-23 | 泰州市艾瑞斯克模具有限公司 | High-temperature sensitive nano-material and preparation method therefor |
| CN111423236A (en) * | 2020-03-22 | 2020-07-17 | 华南理工大学 | (Hf) 0.25Ti0.25Zr0.25W0.25) N high-entropy ceramic powder and preparation method thereof |
| CN112218922A (en) * | 2018-06-27 | 2021-01-12 | 巴斯夫欧洲公司 | Polyol-containing sinter powder for producing moldings |
| CN114605164A (en) * | 2022-03-07 | 2022-06-10 | 南方科技大学 | Porous Ti-Al-N material and preparation method and application thereof |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6059195B2 (en) * | 1982-05-14 | 1985-12-24 | 富士ダイス株式会社 | Manufacturing method of hard sintered material with excellent wear resistance and toughness |
| CA2049636A1 (en) * | 1990-08-31 | 1992-03-01 | Sergej T. Buljan | Ceramic-metal articles and methods of manufacture |
-
2001
- 2001-07-03 JP JP2001202139A patent/JP4105410B2/en not_active Expired - Lifetime
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2002
- 2002-06-27 CN CN 200510087663 patent/CN1724469A/en active Pending
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN101255060B (en) * | 2008-03-26 | 2010-09-08 | 重庆大学 | Method for preparing diffusion couple by using powder |
| CN103975414A (en) * | 2012-07-03 | 2014-08-06 | 株式会社东芝 | Tungsten alloy part, and discharge lamp, transmitting tube and magnetron using same |
| CN103975414B (en) * | 2012-07-03 | 2017-03-08 | 株式会社东芝 | Tungsten alloy part and the discharge lamp using this tungsten alloy part, transmitting tube and magnetron |
| CN105970065A (en) * | 2016-05-31 | 2016-09-28 | 合肥正浩机械科技有限公司 | Cubic boron nitride-carbonyl nickel powder metal ceramic sealing ring and preparation method thereof |
| WO2019095715A1 (en) * | 2017-11-15 | 2019-05-23 | 泰州市艾瑞斯克模具有限公司 | High-temperature sensitive nano-material and preparation method therefor |
| CN112218922A (en) * | 2018-06-27 | 2021-01-12 | 巴斯夫欧洲公司 | Polyol-containing sinter powder for producing moldings |
| CN112218922B (en) * | 2018-06-27 | 2024-03-12 | 巴斯夫欧洲公司 | Polyol-containing sintered powder for producing molded bodies |
| CN111423236A (en) * | 2020-03-22 | 2020-07-17 | 华南理工大学 | (Hf) 0.25Ti0.25Zr0.25W0.25) N high-entropy ceramic powder and preparation method thereof |
| CN111423236B (en) * | 2020-03-22 | 2021-05-14 | 华南理工大学 | (Hf)0.25Ti0.25Zr0.25W0.25) N high-entropy ceramic powder and preparation method thereof |
| CN114605164A (en) * | 2022-03-07 | 2022-06-10 | 南方科技大学 | Porous Ti-Al-N material and preparation method and application thereof |
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| JP2003013102A (en) | 2003-01-15 |
| JP4105410B2 (en) | 2008-06-25 |
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